Bainite wire rod and wire for drawing and methods of producing the same

ABSTRACT

This invention provides bainite wire rod and wire excellent in drawability and methods of producing the same. 
     The bainite wire rod or wire is characterized in that it contains, in weight percent, C: 0.80-0.90%, Si: 0.10-1.50% and Mn: 0.10-1.00%, if required contains Cr: 0.10-1.00%, and is limited to P: not more than 0.02%, S: not more than 0.01% and A1: not more than 0.003%, the remainder being Fe and unavoidable impurities, and has tensile strength and reduction of area determined by the following equations (1) and (2), 
     
         TS≦85×(C)+60                                  (1) 
    
     
         RA≧-0.875×(TS)+158                            (2) 
    
     where 
     C: carbon content (wt%), 
     TS: tensile strength (kgf/mm 2 ), and 
     RA: reduction of area (%).

TECHNICAL FIELD

This invention relates to bainite wire rod and wire for drawing and methods of producing the same.

In this invention, "wire rod," when termed as a product, means wire rod processed for drawing by subjecting it to direct heat treatment immediately after rolling from a steel slab, while, "wire," when termed as a product, means wire subjected to heat treatment in preparation for drawing before drawing or after hot rolling and wire subjected to heat treatment for secondary drawing after being subjected to primary drawing by cold working following hot rolling.

BACKGROUND ART

Wire rod and wire are ordinarily drawn into final products matched to the purpose of use. Before conducting the drawing process, however, it is necessary to put the wire rod or wire in a condition for drawing.

In the case of high-carbon steel wire rod or wire, the prior art requires that a mixed texture of uniform, fine pearlite and a small amount of pro-eutectoid ferrite be established before drawing, and, therefore, a special wire rod or wire heat treatment called "patenting" is conducted. This treatment heats the wire rod or wire to the austenite formation temperature and then cools it at an appropriate cooling rate to complete pearlite transformation, thereby establishing a mixed texture of fine pearlite and a small amount of pro-eutectoid ferrite.

In the wire rod production method of Japanese Patent Publication No. Sho 60-56215, a heat treatment is conducted for obtaining a mixed texture of fine pearlite and a small amount of pro-eutectoid ferrite by immersing the wire rod heated to the austenite formation temperature in molten salt and then cooling it from 800°-600° C. at a cooling rate of 15°-100° C./sec.

However, pearlite texture involves the problems of ductility degradation during drawing at a high reduction of area and of cracking in twist test (hereinafter referred to as "delamination").

The object of this invention is to provide bainite wire rod or wire excellent in ductility and not giving rise to the foregoing problems during drawing, and to provide methods of producing the same.

DISCLOSURE OF THE INVENTION

For achieving this object, the present invention provides bainite-texture wire rod or wire having a chemical composition containing C, Mn, Si, and, if required, further containing Cr in an amount specified by the invention, the upper limit value of P and S content being restricted, and further having prescribed tensile strength and reduction of area.

For achieving this object, the present invention also provides bainite wire rod or wire by increasing the cooling rate up to the nose position in the TTT diagram during cooling of wire rod after hot rolling or during heat treatment of wire after heat treatment at austenite formation temperature, thereby preventing formation of pearlite texture, and then isothermally holding the wire rod or wire at 350°-500° C. In other words, following rolling of the wire rod or heating of the steel wire it is cooled from the temperature range of 1100°-755° C. to the temperature range of 350°-500° C. at a cooling rate of 60°-300° C./sec and maintained at this temperature for at least a specified period to suppress formation of micromartensite texture and thus provide bainite-texture wire rod or wire excellent in drawability, whereby there is obtained wire rod or wire excellent in drawability even at a high reduction of area.

Specifically, the gist of the invention is as set out below.

(1) Bainite wire rod or wire for drawing characterized in that

it contains, in weight percent,

C: 0.80-0.90%,

Si: 0.10-1.50% and

Mn: 0.10-1.00%,

is limited to

P: not more than 0.02%,

S: not more than 0.01% and

Al: not more than 0.003%,

the remainder being Fe and unavoidable impurities, and has tensile strength and reduction of area determined by the following equations (1) and (2),

    TS≦85×(C)+60                                  (1)

    RA≧-0.875×(TS)+158                            (2)

where

C: carbon content (wt%),

TS: tensile strength (kgf/mm²), and

RA: reduction of area (%).

(2) Bainite wire rod or wire for drawing according to paragraph 1 above characterized in that it further contains Cr: 0.10-1.00% as an alloying component.

(3) Bainite wire rod or wire for drawing according to paragraph 1 or 2 above characterized in that it has a microstructure of not less than 80% upper bainite texture in terms of area ratio and an Hv of not more than 450.

(4) A method of producing bainite wire rod for drawing characterized by

rolling into wire rod a steel slab of a composition which

contains, in weight percent,

C: 0.80-0.90%,

Si: 0.10-1.50% and

Mn: 0.10-1.00%,

is limited to

P: not more than 0.02%,

S: not more than 0.01% and

Al: not more than 0.003%,

the remainder being Fe and unavoidable impurities,

cooling the rolled wire rod from the temperature range of 1100°-755° C. to the temperature range of 350°-500° C. at a cooling rate of 60°-300° C./sec, and

holding it in this temperature range for not less than a period of Y sec determined by the following equation (3),

    Y=exp (19.83-0.0329×T)                               (3)

where

T: heat treatment temperature (°C.).

(5) A method of producing bainite wire rod for drawing according to paragraph 4 above wherein the starting steel slab further contains Cr: 0.10-1.00% as an alloying component.

(6) A method of producing bainite wire for drawing characterized by

heating to the temperature range of 1100°-755° C. wire of a composition which

contains, in weight percent,

C: 0.80-0.90%,

Si: 0.10-1.50% and

Mn: 0.10-1.00%,

is limited to

P: not more than 0.02%,

S: not more than 0.01% and

Al: not more than 0.003%,

the remainder being Fe and unavoidable impurities,

cooling the heated wire to the temperature range of 350°-500° C. at a cooling rate of 60°-300° C./sec, and

holding it in this temperature range for not less than a period of Y sec determined by the following equation (3),

    Y=exp(19.83-0.0329×T)                                (3)

where

T: heat treatment temperature (°C.).

(7) A method of producing bainite wire for drawing according to paragraph 6 above wherein the starting wire further contains Cr: 0.10-1.00% as an alloying component.

BRIEF DESCRIPTION OF DRAWING

FIG. 1 is a diagram showing a heat treatment pattern of the present invention.

BEST MODE FOR CARRYING OUT THE INVENTION

The reasons for the restrictions on the constituent elements of the invention will now be discussed.

The reasons for the restrictions on the chemical compositions of the starting steel slab and wire will be described in the following.

Since primary ductility decreases markedly when C content is less than 0.80 wt%, the lower limit of C content is set at 0.80 wt%, while the upper limit of C content is set at 0.90 wt% because central segregation occurs when C is added in excess of 0.90 wt%.

Si is added at not less than 0.10 wt% as a deoxidizing agent. Si is also an element which solid-solution hardens the steel and is further capable of reducing wire relaxation. However, since addition in excess of 1.50 wt% reduces the amount of scale formation, degrading mechanical scaling property, and also lowers the lubricity somewhat, the upper limit of Si content is set at 1.50 wt%.

Mn is added at not less than 0.10 wt% as a deoxidizing agent. Although Mn is an element which strengthens the steel by its presence in solid solution, increasing the amount added increases the likelihood of segregation at the center portion of the wire rod. Since the hardenability of the segregated portion increases, shifting the finishing time of transformation toward the long period side, the untransformed portion becomes martensite, leading to wire breakage during drawing. The upper limit of Mn content is therefore set at 1.00 wt%.

In the case of a hypereutectoid steel such as that of this invention, a cementite network easily forms in the texture following parenting and thick cementite precipitates readily occur. For achieving high strength and high ductility in the steel of this invention, it is necessary to eliminate the aforesaid cementite network and the thick cementite. Since Cr suppresses the appearance of such abnormal cementite portions and has the further effect of making the pearlite fine, it is preferably added as required. The lower limit of Cr content is therefore set at 0.10 wt%, at which these effects can be anticipated. However, addition of a large amount of Cr increases the dislocation density in the ferrite following heat treatment and thus markedly degrades the ductility of the ultra-fine wire following drawing. The upper limit of Cr is therefore set at 1.00 wt%, at which it does not degrade ductility.

Since P and S precipitate at the grain boundaries and degrade the steel properties, it is necessary to hold their contents as low as possible. The upper limit of P content is set at 0.02 wt% and the upper limit of S content is set at 0.01 wt%.

Presence of nonductile inclusions whose main component is Al₂ O₃, such as Al₂ 0₃, MgO--Al₂ O₃ and the like, is a cause for reduction of ultra-file wire ductility. In this invention, therefore, Al content is set at not more than 0.003 wt% for avoiding ductility reduction by nonductile inclusions.

The rolling conditions and heat treatment conditions for obtaining the bainite wire rod and wire of this invention will now be discussed.

The reason for defining the temperature from which cooling is started following wire rod rolling and the wire heating temperature as 755°-1100° C. is that 755° C. is the lower limit temperature of austenitic transformation while abnormal austenite grain growth occurs when the temperature exceeds 1100° C.

The reason for defining the cooling rate from the start of wire rod or wire cooling to the isothermal holding temperature range of 350°-500° C. as 60°-300° C./sec is that 60° C./sec is the lower limit of the critical cooling rate for formation of the upper bainite texture while 300° C./sec is the upper limit of the industrially feasible cooling rate.

The reason for setting the isothermal holding temperature following cooling as 350°-500° C. is that 350° C. is the lower limit temperature for upper bainite texture formation while 500° C. is the upper limit temperature for upper bainite texture formation.

The required isothermal holding time in the temperature range between 350°-500° C. is calculated from the transformation finishing time line in the TTT diagram. If the immersion time in the cooling tank is insufficient, however, martensite forms and becomes a cause for wire breakage during drawing. Since holding for not less than the finishing time of transformation is therefore required, the holding time in the temperature range of 350°-500° C. is defined as the time Y sec determined by the following equation (3).

    Y=exp(19.83-0.0329×T)                                (3)

where

T: heat treatment temperature (°C.).

The reasons for the limitations on the characteristics of the wire rod and wire which are products of the invention will now be discussed.

Since tensile strength is strongly dependent on C content, it is given in terms of its relationship with C content in the manner of equation (1). In wire rod or wire having bainite texture, the cementite precipitation is coarser than it is in prior art wire rod and wire having pearlite texture and, therefore, the tensile strength is lower for the same composition. In wire-drawing, lowering the initial tensile strength improves the drawability and enables drawing to a high reduction of area. The tensile strength is therefore limited in the manner of equation (1) as the limit up to which the drawability is not degraded. When the upper limit is exceeded, the drawability is degraded, causing the occurrence of breakage or delamination in the course drawing.

The reduction of area is an important factor indicative of ease of processing during drawing. Even at the same tensile strength, raising the reduction of area lowers the work hardening rate and enables drawing to a high reduction of area. In wire rod having bainite texture, the cementite precipitation is coarser than it is in prior art wire rod having pearlite texture and, therefore, the reduction of area is higher for the same tensile strength. The reduction of area is therefore limited in the manner of equation (2) as the limit up to which the drawing limit is not degraded. When the lower limit is not reached, the drawability is degraded, causing the occurrence of breakage or delamination in the course drawing.

In addition to having the tensile strength and reduction of area prescribed in the foregoing, the invention wire rod or wire having bainite texture further has a microstructure of not less than 80% upper bainite texture in terms of area ratio and an Hv of not more than 450. As a result, its drawability is even further enhanced.

EXAMPLES Example 1

Table 1 shows the chemical compositions of tested steel specimens.

A-D in Table 1 are invention steels and E and F are comparison steels.

Steel E has a C content exceeding the upper limit and steel F has a Mn content exceeding the upper limit.

The specimens were produced by casting 300×500 mm slabs with a continuous casting machine and then bloom pressing them into 122--mm square slabs.

After these slabs had been rolled into billets, they were rolled into wire rods of the diameters shown in Table 2 and subjected to DLP (Direct Lead Patenting) cooling.

The wire rods were drawn to 1.00 mmφ at an average reduction of area of 17% and subjected to tensile test and twist test.

The tensile test was conducted using the No. 2 test piece of JISZ2201 and the method described in JISZ2241.

In the twist test, the specimen was cut to a test piece length of 100d+100 and rotated at a rotational speed of 10 rpm between chucks spaced at 100 d. d represents the wire diameter.

The characteristic values obtained in this manner are also shown in Table 2.

No. 5--No. 10 are comparative steels.

In No. 5, pearlite which formed because the cooling rate was too slow reduced the drawability, leading to breakage during drawing.

In No. 6, pearlite which formed because the isothermal transformation temperature was too high reduced the drawability, leading to breakage during drawing.

In No. 7, martensite which formed because the isothermal transformation treatment time was short reduced the drawability, leading to breakage during drawing.

In No. 8, bainite texture did not form because the temperature from which cooling was started was too low, reducing the drawability and leading to breakage during drawing.

In No. 9, pearlite which formed because the C content was too high reduced the drawability.

In No. 10, micromartensile which formed in conjunction with central segregation caused by an excessively high Mn content reduced the drawability.

                  TABLE 1     ______________________________________     Chemical Compositions of Tested Steel Specimens     Chemical Compositions (wt %)     Symbol           C      Si     Mn   P    S    Cr   Al   Remark     ______________________________________     A     0.85   0.80   0.80 0.006                                   0.008                                        --   0.002                                                  Invention     B     0.86   0.50   0.60 0.006                                   0.008                                        0.20 0.002                                                  Invention     C     0.85   0.46   0.60 0.006                                   0.007                                        0.25 0.001                                                  Invention     D     0.80   0.20   0.35 0.005                                   0.008                                        0.30 0.002                                                  Invention     E     1.30   0.25   0.40 0.005                                   0.008                                        0.11 0.001                                                  Comparison     F     0.85   0.30   1.50 0.006                                   0.007                                        0.11 0.002                                                  Comparison     ______________________________________

                                      TABLE 2     __________________________________________________________________________     Wire Rod Rolling Conditions and Characteristic Values of Tested Steel     Specimens                               Rolled wire rod                                              After drawing (diameter: 1.00                                              mm)                        Cooling tank                               TS Reduc-                                      Bainite TS Reduc-                                                     Twist             Diameter                  T.sub.0                     V.sub.1                        T.sub.1                            t.sub.1                               kgf/                                  tion                                      texture kgf/                                                 tion                                                     value                                                         Delami-     No.        Symbol             mm φ                  °C.                     °C./s                        °C.                            s  mm.sup.2                                  %   ratio %                                          Hv  mm.sup.2                                                 %   (times)                                                         nation                                                              Remark     __________________________________________________________________________     1  A    4.0  950                     120                        450 160                               130                                  50  95  390 250                                                 45  26  No   Invention     2  B    4.5  1000                     150                        470 100                               125                                  53  90  370 280                                                 42  31  No   Invention     3  C    5.0  1050                     200                        480 70 128                                  58  90  380 290                                                 43  26  No   Invention     4  D    5.5  800                     160                        490 50 125                                  55  85  370 300                                                 41  28  No   Invention     5  A    5.5  1000                     50 450 160                               160                                  25  30  500 Broke at 1.3 mm                                                              Comparison     6  B    5.0  1050                     130                        550 50 150                                  46  50  480 Broke at 1.2 mm                                                              Comparison     7  C    5.5  1100                     120                        490 20 145                                  15  60  470 Broke at 1.4 mm                                                              Comparison     8  D    5.5  740                     120                        480 60 145                                  45  0   460 Broke at 1.3 mm                                                              Comparison     9  E    5.5  1050                     130                        480 80 170                                  35  70  550 290                                                 20  13  Yes  Comparison     10 F    5.5  1050                     120                        470 80 140                                  13  60  470 270                                                 35  19  Yes  Comparison     __________________________________________________________________________      T.sub.0 : Cooling start temperature      V.sub.1 : Cooling rate      T.sub.1 : Holding temperature after cooling      t.sub.1 : Holding time after cooling

Example 2

Table 3 shows the chemical compositions of tested steel specimens.

A-D in Table 3 are invention steels and E and F are comparison steels.

Steel E has a C content exceeding the upper limit and steel F has a Mn content exceeding the upper limit.

The wires were transformed to austenitic texture under the conditions shown in Table 4. After heat treatment they were drawn to 1.00 mmφ at an average reduction of area of 17% and subjected to tensile test and twist test.

The tensile test was conducted using the No. 2 test piece of JISZ2201 and the method described in JISZ2241.

In the twist test, the specimen was cut to a test piece length of 100d+100 and rotated at a rotational speed of 10 rpm between chucks spaced at 100 d. d represents the wire diameter.

The characteristic values obtained in this manner are also shown in Table 4.

No. 1-No. 4 are invention steels. Since they satisfy all heat treatment conditions of the invention, they can be drawn into wire that does not exhibit delamination even at 1.00 mmφ following drawing.

No. 5-No. 10 are comparative steels.

In No. 5, pearlite which formed because the cooling rate was too slow reduced the drawability, leading to breakage during drawing.

In No. 6, pearlite which formed because the isothermal transformation temperature was too high reduced the drawability, leading to breakage during drawing.

In No. 7, martensite which formed because the isothermal transformation treatment time was short reduced the drawability, leading to breakage during drawing.

In No. 8, the bainite texture ratio was zero because the heating temperature was too low, reducing the drawability and leading to breakage during drawing.

In No. 9, pearlite which formed because the C content was too high reduced the drawability.

In No. 10, pearlite formed and the reduction of area was low because the Mn content was too high, reducing the drawability.

                  TABLE 3     ______________________________________     Chemical Compositions of Tested Steel Specimens     Chemical Compositions (wt %)     Symbol           C      Si     Mn   P    S    Cr   Al   Remark     ______________________________________     A     0.85   0.80   0.80 0.006                                   0.008                                        --   0.002                                                  Invention     B     0.86   0.50   0.60 0.006                                   0.008                                        0.20 0.002                                                  Invention     C     0.85   0.46   0.60 0.006                                   0.007                                        0.25 0.001                                                  Invention     D     0.80   0.20   0.35 0.005                                   0.008                                        0.30 0.002                                                  Invention     E     1.30   0.25   0.40 0.005                                   0.008                                        0.11 0.001                                                  Comparison     F     0.85   0.30   1.50 0.006                                   0.007                                        0.11 0.002                                                  Comparison     ______________________________________

                                      TABLE 4     __________________________________________________________________________     Wire Heat Treatment Conditions and Characteristic Values of Tested Steel     Specimens                               After heat treatment,                               before drawing After drawing (diameter: 1.00                                              mm)                        Cooling tank                               TS Reduc-                                      Bainite TS Reduc-                                                     Twist             Diameter                  T.sub.0                     V.sub.1                        T.sub.1                            t.sub.1                               kgf/                                  tion                                      texture kgf/                                                 tion                                                     value                                                         Delami-     No.        Symbol             mm φ                  °C.                     °C./s                        °C.                            s  mm.sup.2                                  %   ratio %                                          Hv  mm.sup.2                                                 %   (times)                                                         nation                                                              Remark     __________________________________________________________________________     1  A    3.0  950                     120                        450 160                               130                                  50  95  390 250                                                 45  26  No   Invention     2  B    4.0  1000                     150                        470 100                               125                                  53  90  370 280                                                 42  31  No   Invention     3  C    4.5  1050                     200                        480 70 128                                  58  90  380 290                                                 43  26  No   Invention     4  D    5.5  800                     160                        490 50 125                                  55  85  370 300                                                 41  28  No   Invention     5  A    5.0  1000                     50 450 160                               160                                  25  30  500 Broke at 1.3 mm                                                              Comparison     6  B    5.0  1050                     130                        550 50 150                                  46  50  480 Broke at 1.2 mm                                                              Comparison     7  C    4.8  1100                     120                        490 20 145                                  15  60  470 Broke at 1.4 mm                                                              Comparison     8  D    5.0  740                     120                        480 60 145                                  45  0   460 Broke at 1.3 mm                                                              Comparison     9  E    4.0  1050                     130                        480 80 170                                  35  70  550 290                                                 20  13  Yes  Comparison     10 F    3.5  1050                     120                        470 80 140                                  13  60  470 270                                                 35  19  Yes  Comparison     __________________________________________________________________________      T.sub.0 : Heating temperature      V.sub.1 : Cooling rate      T.sub.1 : Holding temperature after cooling      t.sub.1 : Holding time after cooling

Industrial Applicability

As discussed in the foregoing, since the wire rod or wire produced in accordance with this invention can be drawn to an appreciably higher reduction of area than possible by the prior art method, it has improved delamination resistance property. The invention is therefore able to provide bainite wire rod and wire that are excellent in drawability. 

We claim:
 1. Bainite wire rod or wire for drawing which consists essentially of, in weight percent,C: 0.80-0.90%, Si: 0.10-1.50% and Mn: 0.10-1.00%,is limited to P: not more than 0.02%, S: not more than 0.01% and Al: not more than 0.003%,the remainder being Fe and unavoidable impurities, and which has a microstructure of not less than 80% upper bainite texture in terms of area ratio and an Hv of not more than 450, and has tensile strength and reduction of area determined by the following equations (1) and (2),

    TS≦85×(C)+60                                  (1)

    RA≧-0.875×(TS)+158                            (2)

where C: carbon content (wt%), TS: tensile strength (kgf/mm²), and RA: reduction of area (%).
 2. Bainite wire rod or wire for drawing according to claim 1 which further consists essentially of Cr: 0.10-1.00% as an alloying component.
 3. A method of producing bainite wire rod for drawing which comprisesrolling into wire rod a steel slab of a composition which contains, in weight percent,C: 0.80-0.90%, Si: 0.10-1.50% and Mn: 0.10-1.00%, is limited toP: not more than 0.02% S: not more than 0.01% and Al: not more than 0.003%, the remainder being Fe and unavoidable impurities, cooling the rolled wire rod from a temperature range of 1100°-755° C. to a temperature range of 350°-500° C. at a cooling rate of 60°-300° C./sec, and holding it in this temperature range for not less than a period of Y sec determined by the following equation (3),

    Y=exp(19.83-0.0329×T)                                (3)

where T: heat treatment temperature (°C.).
 4. A method of producing bainite wire rod for drawing according to claim 3 wherein the starting steel slab further contains Cr: 0.10-1.00% as an alloying component.
 5. A method of producing bainite wire for drawing which comprisesheating to a temperature range of 1100°-755° C. wire of a composition which contains, in weight percent,C: 0.80-0.90%, Si: 0.10-1.50% and Mn: 0.10-1.00%, is limited toP: not more than 0.02%, S: not more than 0.01% and Al: not more than 0.003%, the remainder being Fe and unavoidable impurities, cooling the heated wire to a temperature range of 350°-500° C. at a cooling rate of 60°-300° C./sec, and holding it in this temperature range for not less than a period of Y sec determined by the following equation (3),

    Y=exp(19.83-0.0329×T)                                (3)

where T: heat treatment temperature (°C.).
 6. A method of producing bainite wire for drawing according to claim 5 wherein the starting wire further contains Cr: 0.10-1.00% as an alloying component. 